CN104508166A - Abrasion-resistant steel plate and manufacturing process therefor - Google Patents

Abrasion-resistant steel plate and manufacturing process therefor Download PDF

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Publication number
CN104508166A
CN104508166A CN201380039743.3A CN201380039743A CN104508166A CN 104508166 A CN104508166 A CN 104508166A CN 201380039743 A CN201380039743 A CN 201380039743A CN 104508166 A CN104508166 A CN 104508166A
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steel plate
steel
wear
thickness
slab
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CN104508166B (en
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植田圭治
三浦进一
石川信行
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JFE Steel Corp
JFE Engineering Corp
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NKK Corp
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Abstract

The purpose of the present invention is to provide: an abrasion-resistant steel plate which exhibits excellent impact-abrasion resistance characteristics and which is suitable for use in construction machinery, shipbuilding, steel tubing, civil engineering, architecture and so on; and a manufacturing process therefor. In view of the problem, this abrasion-resistant steel plate is characterized in that: the steel plate has a specific steel composition; the DI* defined by formula (1) is 100 to 250; the surface layers of the plate comprise at least 90% of martensite in area fraction and exhibit a Brinell hardness of 450HBW10/3000 or more; and the thicknesswise central zone of the plate comprises at least 70% of lower bainite in area fraction, the thicknesswise central zone being a zone which spreads from the position corresponding to one half of the plate thickness to the positions corresponding to depths of 0.5mm from both surfaces. DI*=33.85 * (0.1*C)0.5 * (0.7*Si+1) * (3.33*Mn+1) * (0.35*Cu+1) * (0.36*Ni+1) * (2.16*Cr+1) * (3*Mo+1) * (1.75*V+1) * (1.5*W+1) ...(1) [wherein the symbols of elements represent the contents (mass%) of the elements respectively].

Description

Wear-resisting steel plate and manufacture method thereof
Technical field
The present invention relates to the thickness of slab being suitable for supplying engineering machinery, shipbuilding, steel pipe, building, building etc. to be greater than 30mm and to be the wear-resisting steel plate of below 150mm, the steel plate of shock-resistant wearing character excellence when particularly the skin section of steel plate and cross-section are exposed to the abrasion environment of impact and manufacture method thereof.
Background technology
For wear resisting steel, be that martensite single phase structure makes wear resistance improve in order to make microtexture, the general solid solution C that increases measures and makes the hardness of martensitic stucture self increase.But, in this case, the cool attenuation of steel plate, degraded toughness.Therefore, the wear resisting steel that low-temperature flexibility, toughness are improved is developed.
Such as, patent documentation 1 relates to thick high hardness high ductility wear-resistant steel and manufacture method thereof, record to obtain uniform high rigidity and high tenacity in thickness of slab direction, to there is 0.20 ~ 0.40%C-Si-Mn-low P-Nb-B system composition and carrying out quench in furnace containing the steel of one or two or more kinds in Cu, Ni, Cr, Mo, V, Ti, Ca and REM, the microtexture of thickness of slab central part is made the martensite subject organization counting more than 6 with the austenitic grain size of ASTM.
Patent documentation 2 relates to wear-resisting steel plate and manufacture method thereof, record in order to ensure wear resistance and the operability at low-temperature region, there is 0.15 ~ 0.30%C-Si-Mn-low P, S-Nb system composition and forming for the satisfied parameter type be made up of the element of one or two or more kinds in Cu, Ni, Cr, Mo, V, Ti and B, reduce steel plate skin section and inner difference of hardness, and make summer when-40 DEG C can be more than 27J than absorbing.
Patent documentation 3 relates to wear-resisting steel plate and the manufacture method thereof of excellent in low temperature toughness, record and carry out quench in furnace to there is 0.23 ~ 0.35%C-Si-Mn-low P, S-Nb-Ti-B system composition and there is the steel formed meeting the parameter type be made up of the element of one or two or more kinds in Cu, Ni, Cr, Mo and V, microtexture being made the martensite subject organization that particle diameter is less than 15 μm, making summer when wear resistance and-20 DEG C can be more than 27J than absorbing.
Patent documentation 4 relates to wear-resisting steel plate and the manufacture method thereof of excellent in low temperature toughness, record there is 0.23 ~ 0.35%C-Si-Mn-low P, S-Cr-Mo-Nb-Ti-B-REM system composition and having after the steel formed meeting the parameter type be made up of the element of one or two or more kinds in Cu, Ni and V is rolled, direct quenching, microtexture being made the martensite subject organization that particle diameter is less than 25 μm, making summer when wear resistance and-20 DEG C can be more than 27J than absorbing.
Patent documentation
Patent documentation 1: Japanese Patent No. 3273404 publication
Patent documentation 2: Japanese Patent No. 4238832 publication
Patent documentation 3: Japanese Patent No. 4259145 publication
Patent documentation 4: Japanese Patent No. 4645307 publication
Summary of the invention
But, when using hot-rolled steel sheet in the iron structure thing, machinery, device etc. of engineering machinery, shipbuilding, steel pipe, building, building etc., sometimes require shock-resistant wearing character.So-called wearing and tearing be at the position of the running of machinery, device etc. because of steel each other or with the continuous contact of the foreign material such as rock and cause steel skin section by the phenomenon reamed.On the other hand, when so-called gouging abrasion is the cushioning material being such as used to ball mill as steel, become with the environment of the foreign material of high load collision high rigidity, the impingement area(s) of steel side be subject to repetition viscous deformation and after embrittlement, occur with crackle, link the wear phenomenon simultaneously produced, be characterised in that and be easy to develop compared with common wearing and tearing.
In addition, there are steel that C measures high martensitic stucture when being subject to the repeated load of impact, form the extremely hard and crisp microtexture that are called as white layer.Its result, the white layer part generation fragility of steel is peeled off, and cannot obtain sufficient shock-resistant abradability, when toughness is lower, be likely that brittle rupture occurs starting point with white layer.
If the shock-resistant wearing character of steel is poor, then not only become the reason of fault of machinery, device, be also maintained as the large danger of the intensity of works with or without method, therefore high-frequency abrading section repairing, to change be inevitable.Therefore, for the steel being applied to the position of wearing and tearing in the environment of impact, the raising of shock-resistant wearing character is required consumingly.In addition, owing to mostly requiring shock-resistant wearing character in machinery, device etc., therefore require to possess this shock-resistant wearing character in the skin section of steel plate and cross-section.
But, in patent documentation 1, wear resisting property when being subject to impact load is not taken in, especially worry that decline, the brittle rupture of the shock-resistant abradability caused occur to be generated by the white layer of the martensitic stucture of high C thickness of slab central part.
In addition, in patent documentation 2, wear resisting property when being subject to impact load is not also taken in, fail to improve the skin section of steel plate and the shock-resistant wearing character of cross-section.In patent documentation 3,4, wear resisting property when being subject to impact load is not also recorded, especially in thickness of slab central part, in the martensitic stucture of high C, the decline of the shock-resistant abradability caused by white layer generates, brittle rupture be inevitable.In addition, owing to mostly requiring shock-resistant wearing character during use in machinery, device etc., therefore require to possess this shock-resistant wearing character in the skin section of steel plate and cross-section.
Therefore, the object of this invention is to provide wear-resisting steel plate and the manufacture method thereof of a kind of skin section of steel plate and the shock-resistant wearing character excellence of cross-section.Here, skin section refers to from steel surface to the degree of depth to be position 1mm.
The present inventor etc. take wear-resisting steel plate as object, in order to excellent shock-resistant wearing character all can be obtained in the skin section of steel plate and cross-section and can obtain the toughness of the excellence as steel plate, to determining that the various principal elements of the chemical composition of steel plate, manufacture method and microtexture conduct in-depth research, its result, obtains following discovery.
I. when steel plate skin section is exposed to the abrasion environment of impact, in order to ensure the shock-resistant wearing character of excellence, the Brinell hardness guaranteeing skin section is needed to be more than 450HBW10/3000.In addition, in order to obtain this Brinell hardness, chemical constitution and hardenability index importantly by strictly managing steel plate are guaranteed hardening capacity and are made steel plate skin section be martensitic stucture.Steel plate skin section is preferably 100% martensitic stucture, but as long as counts the martensitic stucture of more than 90% just enough with Line Integral rate.Except martensite, carbide etc. also likely containing lower bainite, upper bainite, cementite, perlite, ferrite, residual austenite or Mo, Ti, Cr etc., if but can guarantee the total of these tissues except martensite count less than 10% with Line Integral rate and the Brinell hardness of skin section for more than 450HBW10/3000, then can obtain sufficient shock-resistant wearing character.
II. in order to ensure the shock-resistant wearing character of steel plate cross-section, the particularly important is the shock-resistant wearing character improved at thickness of slab central part.At thickness of slab central part, cause element denseization such as C, Mn, P, S due to center segregation, be therefore easy to become the high high C martensitic stucture of hardness, and be easy to generate the non-metallic inclusions such as MnS.By reducing center segregation, non-metallic inclusion, and the microtexture of thickness of slab central part being made lower bainite main body, improving in the shock-resistant wearing character of thickness of slab central part.This is because the generation of the white layer via non-metallic inclusion making shock-resistant abradability decline is suppressed, also prevents with the stripping of white layer thus, chap as the generation of the crackle of starting point.Here, thickness of slab central part refer to 1/2 position of thickness of slab for benchmark to table in direction be respectively 0.5mm till region.
The present invention is studied further the discovery obtained and is made.
That is, the present invention is:
1. a wear-resisting steel plate, it is characterized in that, there is following steel composition: in mass %, containing C:0.25 ~ 0.33%, Si:0.1 ~ 1.0%, Mn:0.40 ~ 1.3%, below P:0.010%, below S:0.004%, below Al:0.06% and below N:0.007%, further containing below Cu:1.5%, below Ni:2.0%, below Cr:3.0%, below Mo:1.5%, one or two or more kinds in below W:1.5% and below B:0.0030%, the DI* represented by (1) formula is 100 ~ 250, remainder is made up of Fe and inevitable impurity,
Be equivalent to be that the skin section at the position 1mm has the martensite counting more than 90% with Line Integral rate from surface of steel plate to the degree of depth, the Brinell hardness of this surface of steel plate is more than 450HBW10/3000, and the thickness of slab central part being equivalent to the position from 1/2 position of the thickness of slab of this steel plate to direction is respectively 0.5mm in table has the lower bainite that the average crystallite particle diameter counting more than 70% with Line Integral rate is less than 25 μm.
DI*＝33.85×(0.1×C) 0 . 5×(0.7×Si+1)×(3.33×Mn+1)×(0.35×Cu+1)×(0.36×Ni+1)×(2.16×Cr+1)×(3×Mo+1)×(1.75×V+1)×(1.5×W+1)···(1)
Each symbol of element is content (quality %)
2. the wear-resisting steel plate of the shock-resistant wearing character excellence as described in above-mentioned 1, is characterized in that, above-mentioned steel composition is in mass % further containing one or two or more kinds in Nb:0.005 ~ 0.025%, V:0.01 ~ 0.1% and Ti:0.005 ~ 0.03%.
3. the wear-resisting steel plate of the shock-resistant wearing character excellence as described in above-mentioned 1 or 2, is characterized in that, above-mentioned steel composition is in mass % further containing one or two or more kinds in below REM:0.02%, below Ca:0.005%, below Mg:0.005%.
4. a manufacture method for wear-resisting steel plate, is characterized in that, after the steel disc that the steel had according to any one of above-mentioned 1 ~ 3 forms is heated to 1000 DEG C ~ 1200 DEG C, carry out hot rolling, the steel plate obtained, to room temperature, thereafter, reheats to Ac by air cooling 3~ 950 DEG C, quench.
5. a manufacture method for wear-resisting steel plate, is characterized in that, after the steel disc that the steel had according to any one of above-mentioned 1 ~ 3 forms is heated to 1000 DEG C ~ 1200 DEG C, at Ar 3after above temperature province carries out hot rolling, by the steel plate that obtains from Ar 3the temperature of ~ 950 DEG C rises quenches.
6. the manufacture method of the wear-resisting steel plate as described in above-mentioned 5, is characterized in that, after above-mentioned quenching, reheats described steel plate to Ac further 3~ 950 DEG C, quench.
According to the present invention, the wear-resisting steel plate of the shock-resistant wearing character excellence of skin section and cross-section can be obtained, contribute to very much improving when steel structure makes manufacturing efficiency, security, industrially play significant effect.
Accompanying drawing explanation
Fig. 1 is the figure of the collection position for illustration of impact wear test sheet.
Fig. 2 is the figure for illustration of impact wear testing machine.
Embodiment
In the present invention, one-tenth to be grouped into and microtexture specifies.
[one-tenth is grouped into]
In below illustrating, % is quality %.
C：0.25～0.33％
C is for improving martensitic hardness and improve hardening capacity and guarantee the important element of excellent wear resistance at thickness of slab central part as the tissue of regulation, in order to obtain its effect, needing containing more than 0.25%.On the other hand, if amount is greater than 0.33%, then not only weldability is deteriorated, and is easy to when being subject to the repeated load of impact generate white layer, promotes the generation of wearing and tearing caused by peeling off or crackle and shock-resistant wearing character is deteriorated.Therefore, be defined in the scope of 0.25 ~ 0.33%.Be preferably 0.26 ~ 0.31%.
Si：0.1～1.0％
Si plays a role as deoxidation material, is not only necessary on steel processed, and has the effect being solid-solubilized in and being made steel plate high rigidity in steel by solution strengthening.In order to obtain this effect, need containing more than 0.1%.On the other hand, if amount is greater than 1.0%, then weldability and toughness are significantly deteriorated, and are therefore defined in the scope of 0.1 ~ 1.0%.Be preferably 0.2 ~ 0.8%.
Mn：0.40～1.3％
Mn has the effect that the hardening capacity of steel is increased, and in order to ensure the hardness of mother metal, needs to be more than 0.40%.On the other hand, if the Mn contained is greater than 1.3%, then not only the toughness of mother metal, ductility and weldability are deteriorated, and encourage the grain boundary segregation of P in center segregation portion, encourage the generation of delayed fracture.In addition, in the amount increase of the MnS that thickness of slab central part generates, and become thick, when steel plate cross-section is exposed to the abrasion environment of impact, stress concentration near MnS, promotes the generation of white layer, and shock-resistant abradability is deteriorated.Therefore, be defined in the scope of 0.40 ~ 1.3%.Be preferably 0.50 ~ 1.2%.
Below P:0.010%
If the P contained is greater than 0.010%, then at grain boundary segregation, become the generation starting point of delayed fracture, and make degraded toughness.Therefore, be set to the upper limit of content by 0.010%, preferably reduce as far as possible.Should illustrate, excessive P reduces makes refining cost surging, is disadvantageous economically, is therefore preferably set to more than 0.002%.
Below S:0.004%
S not only makes low-temperature flexibility, the ductility deteriorates of mother metal, and increase in the amount of the MnS of thickness of slab central part generation and become thick, when steel plate cross-section is exposed to the abrasion environment of impact, stress concentration near MnS, promote the generation of white layer, shock-resistant abradability is deteriorated.Therefore, preferably reduce 0.004% as the upper limit.
Below Al:0.06%
Al plays a role as reductor, the most universally uses in the molten steel deacidifying process of steel plate.In addition, form AlN by being fixed by the solid solution N in steel, there is the effect of the coarsening suppressing crystal grain, and there is the effect of the generation of degraded toughness and the delayed fracture suppressed caused by solid solution N reduces.On the other hand, if the Al contained is greater than 0.06%, then at AlN and Al that thickness of slab central part generates 2o 3amount increase, and become thick, when steel plate cross-section is exposed to the abrasion environment of impact, at AlN and Al 2o 3neighbouring stress concentration, promotes the generation of white layer, and shock-resistant abradability is deteriorated.Therefore, less than 0.06% is defined in.
Below N:0.007%
N is contained in steel as inevitable impurity, if amount is greater than 0.007%, then increase in the amount of the AlN of thickness of slab central part generation, and become thick, when steel plate cross-section is exposed to the abrasion environment of impact, stress concentration near AlN, promotes the generation of white layer, and shock-resistant abradability is deteriorated.Therefore, less than 0.007% is defined in.
One or two or more kinds in Cu, Ni, Cr, Mo, W and B
Cu, Ni, Cr, Mo, W and B are and improve hardening capacity and the element contributing to the hardness improving steel, can correspond to desired intensity and suitably contain.
When adding Cu, preferably content is set to more than 0.05%, if but be greater than 1.5%, then produce the surface texture variation of red brittleness and steel plate, be therefore set to less than 1.5%.
When adding Ni, preferably content is set to more than 0.05%, if but be greater than 2.0%, then effect is saturated, unfavorable economically, is therefore set to less than 2.0%.
When adding Cr, be preferably set to more than 0.05%, if but be greater than 3.0%, then toughness and weldability decline, and are therefore set to less than 3.0%.
Mo makes hardening capacity increase significantly and to the effective element of the high rigidityization of mother metal.In order to obtain this effect, preferably content is set to more than 0.05%, if but be greater than 1.5%, then to the anti-thread breakage generation detrimentally affect of base metal tenacity, ductility and proper alignment, be therefore set to less than 1.5%.
W makes hardening capacity increase significantly and to the effective element of the high rigidityization of mother metal.In order to obtain this effect, preferably content is set to more than 0.05%, if but be greater than 1.5%, then to the anti-thread breakage generation detrimentally affect of base metal tenacity, ductility and proper alignment, be therefore set to less than 1.5%.
B makes hardening capacity increase significantly and to the effective element of the high rigidityization of mother metal with the interpolation of trace.In order to obtain this effect, preferably content is set to more than 0.0003%, if but be greater than 0.0030%, then to the anti-thread breakage generation detrimentally affect of base metal tenacity, ductility and proper alignment, be therefore set to less than 0.0030%.
DI*＝33.85×(0.1×C) 0 . 5×(0.7×Si+1)×(3.33×Mn+1)×(0.35×Cu+1)×(0.36×Ni+1)×(2.16×Cr+1)×(3×Mo+1)×(1.75×V+1)×(1.5×W+1)：100～250
DI* be skin section in order to make mother metal more than 90% for martensite and make thickness of slab central part be organized as with Line Integral rate count more than 70% lower bainite and the value that there is excellent wear resistance and specify, therefore the value of DI* is set to 100 ~ 250.When being less than 100, the depth of hardening from thickness of slab top layer shoals, and cannot obtain desired microtexture, as the lifetime of wear resisting steel at thickness of slab central part.On the other hand, if be greater than 250, then toughness, delayed fracture characteristic are significantly deteriorated.Therefore, the scope of 100 ~ 250 is set to.Preferably be set to the scope of 120 ~ 230.
Be more than basal component of the present invention composition, remainder be set to Fe and inevitable impurity.
In addition, in the present invention, in order to improve characteristic further, except above-mentioned basal component system, can also containing one or two or more kinds in Nb, V, Ti, REM, Ca and Mg.
Nb：0.005～0.025％
Nb makes microtexture miniaturization as Carbonitride Precipitation, and is fixed by solid solution N and have both the element of effect of the generation improving toughness and suppress delayed fracture.In order to obtain this effect, need the content of more than 0.005%.On the other hand, if amount is greater than 0.025%, then separate out thick carbonitride, promote the generation of white layer, shock-resistant abradability is deteriorated.Therefore, be defined in the scope of 0.005 ~ 0.025%.
V：0.01～0.1％
V makes microtexture miniaturization as Carbonitride Precipitation, and is fixed by solid solution N and have both the element of effect of the generation improving toughness and suppress delayed fracture.In order to obtain this effect, need the content of more than 0.01%.On the other hand, if amount is greater than 0.1%, then separate out thick carbonitride, promote the generation of white layer, shock-resistant abradability is deteriorated.Therefore, be defined in the scope of 0.01 ~ 0.1%.
Ti：0.005～0.03％
Ti forms TiN by being fixed by solid solution N, has the effect suppressing coarse grains, and has the effect of the generation of degraded toughness and the delayed fracture suppressed caused by solid solution N reduces.In order to obtain these effects, need the content of more than 0.005%.On the other hand, if amount is greater than 0.03%, then separate out thick carbonitride, promote the generation of white layer, shock-resistant abradability is deteriorated.Therefore, be defined in the scope of 0.005 ~ 0.03%.
REM, Ca and Mg all contribute to improving toughness, selectively add according to desired characteristic.
Add REM time, preferably content is set to more than 0.002%, even if but owing to being greater than 0.02%, effect also can be saturated, therefore with 0.02% for the upper limit.
Add Ca time, preferably content is set to more than 0.0005%, even if but owing to being greater than 0.005%, effect also can be saturated, therefore with 0.005% for the upper limit.
Add Mg time, preferably content is set to more than 0.001%, even if but owing to being greater than 0.005%, effect also can be saturated, therefore with 0.005% for the upper limit.
[microtexture]
In the present invention, improve to make the shock-resistant wearing character of cross-section, for in the position of 1/2 position of the thickness of slab from steel plate to direction is respectively 0.5mm in table and the microtexture of steel plate of thickness of slab central part, there is the average crystallite particle diameter counting more than 70% with Line Integral rate counts less than 25 μm lower bainite with equivalent diameter.
Here, if average crystallite particle diameter is greater than 25 μm in equivalent diameter, then cause the decline of toughness, the generation of delayed fracture.In addition, if containing martensite as the tissue except lower bainite, then via the existence of non-metallic inclusion etc., encourage the generation of white layer, crackle produces, and shock-resistant abradability is deteriorated, if but less than 10%, then can ignore its impact.In addition, when there is upper bainite, ferrite, perlite etc., hardness declines, and shock-resistant abradability is deteriorated, if but less than 20%, then can ignore its impact.
In addition, be equivalent to from the view point of the skin section at the position of above-mentioned steel surface to degree of depth 1mm from shock-resistant wearing character, there is the martensitic stucture counting more than 90% with Line Integral rate.By forming the martensitic stucture of more than 90% and making the surface hardness of steel plate count more than 450HBW10/3000 with Brinell hardness, excellent shock-resistant wearing character can be guaranteed.Should illustrate, the observational technique of microtexture explains in an embodiment.
[hardness of steel plate skin section]
When the surface hardness of steel plate is less than 450HBW10/3000 with Brinell tester, shock-resistant wearing character is insufficient, as the lifetime of wear resisting steel.Therefore, surface hardness is set to more than Brinell tester 450HBW10/3000.
[manufacture method of wear-resisting steel plate]
Wear resisting steel involved in the present invention can be manufactured by following manufacturing condition.
In explanation, represent the temperature of 1/2 position referred at thickness of slab with " DEG C " of temperature correlation.
First, by the molten steel of above-mentioned composition by known melting method melting, such as, by Continuous casting process or ingot casting-split rolling method method etc., the steel raw materials such as the slab of specified dimension are obtained.
After the steel raw material obtained just is cast not carrying out cooling or reheat to 1000 ~ 1200 DEG C immediately after temporarily cooling, thereafter, hot rolling and make the steel plate of desired thickness of slab.Reheat temperature when being less than 1000 DEG C, resistance to deformation during hot rolling uprises, and cannot obtain every time large draught, and therefore rolling pass number increases, cause the decline of rolling efficiency, and sometimes cannot crimp the casting flaw in steel raw material (slab).On the other hand, if reheat temperature to be greater than 1200 DEG C, then due to the dirt (scale) during heating, easily produce surface spots, the processing burden after rolling increases.Therefore, reheat by steel raw material the scope that temperature is set to 1000 ~ 1200 DEG C.
Hot rolling is implemented, till becoming target thickness of slab to the steel raw material be reheated.As long as the satisfied thickness of slab as target of hot-rolled condition and shape, there is no particular limitation for its condition.But, when thickness of slab is greater than the pole Plate Steel of 70mm, in order to hole crimping, preferably every time draft be more than 15% rolling pass guarantee more than at least 1 passage.Rolling end temp is preferably set to Ar 3above.
Rolling end temp is less than Ar 3time, resistance to deformation uprises, and therefore rolling load increases, and becoming large, dropping to Ar to make Plate Steel to the burden of roller mill 3following rolling temperature, needs in rolling midway standby, hinders productivity significantly.
After hot rolling terminates, air cooling, carries out quench in furnace process, or hot rolling terminate after carry out direct quenching at once.
When carrying out quench in furnace process after rolling terminates, reheat to Ac 3~ 950 DEG C, after keeping certain hour, quench.If Heating temperature is greater than 950 DEG C, then surface of steel plate proterties is deteriorated, and coarsening, toughness and delayed fracture properties deteriorate.
Hold-time does not specify especially, if be greater than 1hr, then causes the degraded toughness of mother metal because of the coarsening of austenite grain, is therefore preferably within 1hr, if the soaking in heat treatment furnace is good, then can keep the short period of time.Should illustrate, Ac 3(DEG C) such as can use deriving containing value with each composition of undefined relational expression input steel:
Ac 3＝854-180C+44Si-14Mn-17.8Ni-1.7Cr
(symbol of element represents the content (quality %) of each element in steel)
When carrying out direct quenching after rolling terminates, at Ar 3above temperature province carries out hot rolling, after rolling terminates, from Ar 3~ 950 DEG C start quenching.
Ar 3(DEG C) such as can use deriving containing value with each composition of undefined relational expression input steel:
Ar 3＝910-310C-80Mn-20Cu-15Cr-55Ni-80Mo
(symbol of element represents the content (quality %) of each element in steel)
Quenching can be carried out the high velocity flow of surface of steel plate inject high pressure, also steel plate can be impregnated in water and carry out.The speed of cooling of thickness of slab 1/2 position of this situation is 20 DEG C/about s when thickness of slab is 35mm, is 10 DEG C/about s when thickness of slab is 50mm, is 3 DEG C/about s when thickness of slab is 70mm.If the speed of cooling of this degree, then thickness of slab central part can be made lower bainite counts more than 70% tissue with Line Integral rate.In addition, when thickness of slab is below 30mm, if quenched by water-cooled, then speed of cooling becomes excessive, thickness of slab central part cannot be made lower bainite counts more than 70% tissue with Line Integral rate.
Also can implement further the steel plate after hot rolling, direct quenching and reheat to Ac 3the quench in furnace process of ~ 950 DEG C.Tissue in Plate Steel is homogenized and miniaturization further, and intensity, the toughness of mother metal improve.
Embodiment
Below, embodiment is described.
By converter-get kettle refining-Continuous casting process, to be prepared into after plate slab that the various one-tenth shown in table 1 are grouped into is heated to 1000 ~ 1200 DEG C with the condition shown in table 2, implement hot rolling, after rolling, direct quenching (DQ) is carried out immediately to a part of steel plate.(RQ) is quenched to reheating after to 900 DEG C through a part of steel plate of direct quenching (DQ).In addition, hot rolling, cooled a part of steel plate are reheated and quench (RQ) after 900 DEG C.
With following main points, structure observation, surface hardness mensuration, base metal tenacity, impact wear test are implemented to the steel plate obtained.
From each steel plate acquisition test sheet, with rolling direction be the thickness of slab (t) in the thickness of slab direction in the cross section of parallel direction 1/2 position, utilize opticmicroscope and transmission electron microscope tissues observed, obtain the median size of tissue point rate (lower bainite point rate) and old austenite grain (old γ grain).Lower bainite does not carry out phase transformation from austenite diffusely with long distance, and therefore the particle diameter of lower bainite is identical with old austenite particle diameter.In addition, lower bainite and martensite roughly can use opticmicroscope, specifically use transmission electron microscope, are differentiated by the difference of the precipitation form of cementite.
It is the surface hardness measured according to JIS Z2243 (1998) under top layer that surface hardness measures.Measure and use the tungsten hard sphere that diameter is 10mm, load is set to 3000kgf.
From the direction vertical with rolling direction of the position of 1/4 of the thickness of slab (t) of each steel plate, V-notch test film is extracted according to the regulation of JIS Z 2202 (1998), according to the regulation of JIS Z 2242 (1998), each steel plate is implemented to the Charpy impact test of 3 samples in each temperature, obtain the absorption energy at 0 DEG C, evaluate base metal tenacity.The absorption of 3 samples can (vE 0) mean value when being more than 30J, be evaluated as the steel plate of base metal tenacity excellence.
Impact wear test is the test film gathering 10mm × 25mm × 75mm as shown in Figure 1 from 1/2 of the thickness of slab (t) in surface of steel plate and steel plate cross section.Test film for examination steel and SS400 is fixed on the rotor of the impact abrasion testing equipment shown in Fig. 2, in cylinder, puts into 1500cm 3100%SiO 2silica (median size 30mm) also, after sealing, rotates with rotor speed 600rpm, drum rotational speed 45rpm, the total revolution 10000 of rotor.
The surface of the test film after terminating with projector's viewing test, the steel plate of the crackle being more than 3mm not have length is anti-thread breakage excellence.And then, be determined at the reduction of the test film weight before and after test.With (the weight reduction of the test film of SS400)/(the weight reduction of the test film of object material) for wear-resistant ratio, the steel plate having more than 2.5 to have more than 3.0 in steel plate skin section, in 1/2 cross-section of thickness of slab (t) is the steel plate of shock-resistant wearing character excellence.
The obtained results are shown in table 3.
As known from Table 3, in example of the present invention, surface hardness has more than 450HBW10/3000, and the base metal tenacity of 0 DEG C has more than 30J, and do not crack in impact wear test, the wear-resistant ratio of SS400 is had to more than 3.0 in steel plate skin section, has more than 2.5 in 1/2t cross-section.
On the other hand, confirm in the comparative example outside the scope of the invention, any one or its in surface hardness, base metal tenacity and impact wear test are multiple cannot meet target capabilities.
[table 1]
[table 2]
[table 2]
Note: underscore is outside scope of the present invention
[table 3]

Claims (6)

1. a wear-resisting steel plate, it is characterized in that, there is following steel composition: in mass %, containing C:0.25 ~ 0.33%, Si:0.1 ~ 1.0%, Mn:0.40 ~ 1.3%, below P:0.010%, below S:0.004%, below Al:0.06% and below N:0.007%, further containing below Cu:1.5%, below Ni:2.0%, below Cr:3.0%, below Mo:1.5%, one or two or more kinds in below W:1.5% and below B:0.0030%, the DI* represented by (1) formula is 100 ~ 250, remainder is made up of Fe and inevitable impurity,
Be equivalent to be that the skin section at the position 1mm has the martensite counting more than 90% with Line Integral rate from surface of steel plate to the degree of depth, the Brinell hardness of this surface of steel plate is more than 450HBW10/3000, the thickness of slab central part being equivalent to the position from 1/2 position of the thickness of slab of this steel plate to direction is respectively 0.5mm in table has the lower bainite that the average crystallite particle diameter counting more than 70% with Line Integral rate is less than 25 μm
DI*＝33.85×(0.1×C) 0.5×(0.7×Si+1)×(3.33×Mn+1)×(0.35×Cu+1)×(0.36×Ni+1)×(2.16×Cr+1)×(3×Mo+1)×(1.75×V+1)×(1.5×W+1)···(1)，
Each symbol of element is content, and its unit is quality %.
2. wear-resisting steel plate as claimed in claim 1, is characterized in that, described steel composition is in mass % further containing one or two or more kinds in Nb:0.005 ~ 0.025%, V:0.01 ~ 0.1% and Ti:0.005 ~ 0.03%.
3. wear-resisting steel plate as claimed in claim 1 or 2, is characterized in that, described steel composition is in mass % further containing one or two or more kinds in below REM:0.02%, below Ca:0.005%, below Mg:0.005%.
4. a manufacture method for wear-resisting steel plate, is characterized in that, after the steel disc that the steel had according to any one of claims 1 to 3 forms is heated to 1000 DEG C ~ 1200 DEG C, carry out hot rolling, the steel plate obtained, to room temperature, thereafter, reheats to Ac by air cooling 3~ 950 DEG C, quench.
5. a manufacture method for wear-resisting steel plate, is characterized in that, after the steel disc that the steel had according to any one of claims 1 to 3 forms is heated to 1000 DEG C ~ 1200 DEG C, at Ar 3after above temperature province carries out hot rolling, by the steel plate that obtains from Ar 3the temperature of ~ 950 DEG C rises quenches.
6. the manufacture method of wear-resisting steel plate as claimed in claim 5, is characterized in that, after described quenching, reheat described steel plate to Ac further 3~ 950 DEG C, quench.
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Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2002080930A (en) * 2000-09-11 2002-03-22 Nkk Corp Wear resistant steel having excellent toughness and delayed fracture resistance and its production method
JP2004300474A (en) * 2003-03-28 2004-10-28 Jfe Steel Kk Abrasion resistant steel and manufacturing method therefor
JP2011214120A (en) * 2010-04-02 2011-10-27 Jfe Steel Corp Wear-resistant steel plate superior in low-temperature-tempering embrittlement crack properties
CA2801703A1 (en) * 2010-06-30 2012-01-05 Jfe Steel Corporation Abrasion resistant steel plate which exhibits excellent weld toughness and excellent delayed fracture resistance
JP2012031511A (en) * 2010-06-30 2012-02-16 Jfe Steel Corp Wear-resistant steel sheet having excellent toughness of multi-layer-welded part and lagging destruction resistance properties
WO2012133910A1 (en) * 2011-03-29 2012-10-04 Ｊｆｅスチール株式会社 Abrasion-resistant steel sheet exhibiting excellent resistance to stress corrosion cracking, and method for producing same

Family Cites Families (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP3273404B2 (en) 1995-10-24 2002-04-08 新日本製鐵株式会社 Manufacturing method of thick high hardness and high toughness wear resistant steel
JP4238832B2 (en) 2000-12-27 2009-03-18 Ｊｆｅスチール株式会社 Abrasion-resistant steel plate and method for producing the same
JP4259145B2 (en) 2003-03-11 2009-04-30 Ｊｆｅスチール株式会社 Abrasion resistant steel plate with excellent low temperature toughness and method for producing the same
JP4645307B2 (en) 2005-05-30 2011-03-09 Ｊｆｅスチール株式会社 Wear-resistant steel with excellent low-temperature toughness and method for producing the same
CN102560272B (en) * 2011-11-25 2014-01-22 宝山钢铁股份有限公司 Ultrahigh-strength abrasion-resistant steel plate and manufacturing method thereof

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2002080930A (en) * 2000-09-11 2002-03-22 Nkk Corp Wear resistant steel having excellent toughness and delayed fracture resistance and its production method
JP2004300474A (en) * 2003-03-28 2004-10-28 Jfe Steel Kk Abrasion resistant steel and manufacturing method therefor
JP2011214120A (en) * 2010-04-02 2011-10-27 Jfe Steel Corp Wear-resistant steel plate superior in low-temperature-tempering embrittlement crack properties
CA2801703A1 (en) * 2010-06-30 2012-01-05 Jfe Steel Corporation Abrasion resistant steel plate which exhibits excellent weld toughness and excellent delayed fracture resistance
JP2012031511A (en) * 2010-06-30 2012-02-16 Jfe Steel Corp Wear-resistant steel sheet having excellent toughness of multi-layer-welded part and lagging destruction resistance properties
WO2012133910A1 (en) * 2011-03-29 2012-10-04 Ｊｆｅスチール株式会社 Abrasion-resistant steel sheet exhibiting excellent resistance to stress corrosion cracking, and method for producing same

Cited By (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN107923023A (en) * 2015-08-21 2018-04-17 Posco公司 High rigidity steel plate and its manufacture method
CN105200335A (en) * 2015-11-07 2015-12-30 李白 Wind power gear for wind driven generator
CN105821316A (en) * 2016-05-23 2016-08-03 安徽鑫宏机械有限公司 Casting method for Ni-B-Si alloy surface modified composite valve body
CN105886917A (en) * 2016-05-23 2016-08-24 安徽鑫宏机械有限公司 Casting method of high-hardness and erosion-resistant combined stop valve body
CN106086637A (en) * 2016-06-15 2016-11-09 宁波市鄞州海胜机械有限公司 A kind of wear-resisting shaft
CN108699652A (en) * 2016-09-15 2018-10-23 新日铁住金株式会社 Abrasion-resistant stee
CN106756530A (en) * 2016-11-17 2017-05-31 哈尔滨光霞金属材料有限公司 High-strength abrasion-proof steel and its application in engineering mechanical components and agricultural machinery part
CN106399843A (en) * 2016-12-05 2017-02-15 郑州丽福爱生物技术有限公司 Wear-resisting alloy material and preparation method thereof
CN109937266A (en) * 2017-06-21 2019-06-25 日本制铁株式会社 Steel plate
CN111511952A (en) * 2017-12-22 2020-08-07 株式会社Posco Wear-resistant steel having excellent hardness and impact toughness and method for manufacturing same
CN111511952B (en) * 2017-12-22 2022-08-16 株式会社Posco Wear-resistant steel having excellent hardness and impact toughness and method for manufacturing same
CN109280852A (en) * 2018-11-12 2019-01-29 南京钢铁股份有限公司 A kind of big thickness NM500 abrasion-resistant stee and production method
CN109385573A (en) * 2018-11-19 2019-02-26 宁波金汇精密铸造有限公司 Brake disc of high-speed train alloy cast steel material and preparation method thereof

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